Polymer composition with uniformly distributed nano-sized inorganic particles

ABSTRACT

The present invention provides a polymer composition wherein inorganic particles are uniformly dispersed at the nano level in the polymer without having said inorganic particles being surface-treated. It further provides a method for manufacturing a polymer composition wherein a co-aggregate which is obtained by uniformly mixing polymer dispersion with an inorganic particle colloidal solution and co-aggregating the polymer primary particles and inorganic particles which are heterogeneous particles, is separated from the solvent and dried so that the inorganic particles are uniformly dispersed at the nano level in the polymer; and the polymer composition which is obtained by said method.

FIELD OF INVENTION

The present invention relates to a polymer composition wherein inorganicparticles are uniformly dispersed at the nano level in a polymer and toa method for manufacturing said polymer composition.

BACKGROUND OF THE INVENTION

A conventional means for improving the properties such as mechanicalstrength, dimensional stability, and compression creep resistance ofpolymers has been to combine a filler with polymer. However, theuniformity with which filler distributed in the polymer is notcompletely specified.

Recently, methods have been developed to improve the mechanicalstrength, heat deformation temperature and dimensional stability ofpolymer by direct melt blending of nano particles such as inorganic nanoparticles into the polymer. However, when inorganic particles aremelt-mixed with polymer, the mutual cohesive force of the particles isfound to increase as particle diameter is decreased and the inorganicparticles tend to aggregate, that is, the inorganic particles clustertogether, especially at when the particles are at the nano level insize, i.e. about 1 to 1000 nm in diameter. Therefore, even when the nanoparticles are directly melt-mixed with the polymer, it is extremelydifficult to disperse the particles at the nano level in the polymer(Powder Body Engineering Handbook, 2nd Edition, p. 291-294, 1983, asreported in the Proceedings of the 47^(th) Meeting of the Japan Societyof Materials Science, Kyoto, Oct. 29-30, 2003, pp. 150-151).

One approach to overcoming the problems of the above described directmelt-mixing method, is a solution-mixing method wherein a colloidalsolution of stably dispersed inorganic particles is mixed with afunctionalized polymer dissolved in a liquid. For example, U.S. RE37,022proposes a composition (coating agent) wherein perfluoropolymer isdissolved in an organosol wherein inorganic particles with an averageparticle diameter of 1000 nm or less, treated with fluorine-containingsurfactant, are dispersed in a fluorinated solvent having no hydrogen(that is, the solvent has no hydrogen atoms bonded to the multivalentatoms of the solvent molecule) or a solvent made by mixing said solventwith a fluorinated solvent that contains hydrogen. The use offunctionalized fluoropolymer and fluorinated solvents make this anexpensive and inconvenient approach, suitable only for specializedapplications.

U.S. Pat. No. 6,350,806 is directed to water-based paint, which is curedat up to 300° C., made of aqueous fluoropolymer dispersion which isadded to aqueous-emulsified acrylate and methacrylate monomer, which arethen polymerized. To the resulting polymer dispersion is mixed drycolloidal silica that is been treated with organoalkoxysilane. In theabsence of the organoalkoxysilane, the silica is not stably mixed andthe paint lacks storage stability. The distribution of the treatedsilica particles in the dried paint coating is not disclosed. Being apaint, the composition is not suitable for compression molded, extrusionmolded, or injection molded articles. In view of the substantial acryliccontent, 30 parts acrylate to 100 parts fluoropolymer, the resultingpolymer composition lacks the thermal properties and oxidativeresistance characteristic of fluoropolymers.

Another approach to the above described direct melt-mixing method isreported in Colloid and Surfaces, vol. 63, p. 103-111, 1992 wherein itis disclosed that aggregate is created from the solution made frommixing heterogeneous particles, wherein a colloidal silica to whichpotassium chloride is added so that the pH value is 5.6, is mixed withpolystyrene emulsion in which the polystyrene is a copolymer thatincludes comonomers that provide acid and base functionality whereby thepolymer is amphoteric. The silica and polystyrene particles haveopposite electrical charge and thus form an unstable mixture, whereinslight mixing causes the particles to form heterocoagulates. Thisreference requires that the ratio of the diameter of the silica primaryparticles to that of the polymer primary particles be 3 or more toobtain the proper aggregate composed of a relatively large silica coreand small amphoteric-modified polystyrene particles clustered around thecore. These aggregates are disclosed to be useful as functionalparticles in industrial fields.

U.S. Patent Application Publication No. 2005/0123739 disclosesdispersing dry mesoporous hydrophobic-modified fused silica intopolytetrafluoroethylene dispersion, which is then coagulated, and theliquid drained, and the coagulate dried at 130° C., followed bycalendering into sheet form, and sintering to improve electricalproperties as printed circuit substrates.

Japanese published examined application No. Hei 7-64936 proposes amethod for obtaining a powder with an average particle diameter of 3 mmwherein a suspension of silicon carbide particles with an averageparticle diameter of 4000 nm that has been surface-treated with anaminosilane group surfactant, is added to a fluoropolymer dispersion.Then nitric acid is added to the mixture to break the emulsion and afterthat, trichlorotrifluoroethane is added to the mixture to coagulate andgranulate the particles thereby obtaining an powder with an averageparticle diameter of 3 mm.

None of the above-mentioned teachings solve the problem of providing amolded article of filled polymer where the filler is nano-sized and isuniformly dispersed as such in the polymer.

SUMMARY OF THE INVENTION

The present invention solves this problem by the method of manufacturingthe polymer composition, comprising mixing aqueous polymer dispersioncomprising polymer primary particles with aqueous colloidal solution ofinorganic particles having an average particle diameter of 1 to 1000 nm,coagulating the resultant mixture to make a co-aggregate of theparticles, separating said co-aggregate from the aqueous media of saidsolution, and drying the coaggregate.

In a preferred method, a polymer dispersion is formed, wherein thepolymer primary particles are surrounded by a surfactant (which mayhereinafter be called emulsifying agent) and stably dispersed in theaqueous medium in the course of emulsion polymerization, is mixed withan aqueous colloidal solution (which may hereinafter be called aninorganic particle sol). Then, after the polymer primary particles areuniformly mixed with the inorganic particles in the mixed aqueous media,the resultant mixture is coagulated so that the uniformly mixed polymerprimary particles and inorganic particles are solidified, i.e.,co-aggregated, to distinguish from aggregates of primary polymerparticles with each other, and aggregates of inorganic particles witheach other. Then, by separating the co-aggregate from the aqueous phaseand drying, dried co-aggregate of the inorganic particles dispersed atthe nano level in the polymer is obtained. The mixture of the inorganicparticle sol with the stably dispersed polymer primary particles resultsin the inorganic particles also being stably dispersed at the nano levelin admixture with the polymer primary particles.

After the polymer primary particles and inorganic particles areuniformly mixed, the resulting mixture is subject to coagulation by suchtechniques a vigorous mechanical mixing (a strong shearing force), byadding electrolyte to the mixture, or by freezing the mixture(dispersion). In this way, the stability of the dispersed admixture ofthe polymer particles and of the inorganic particles is decreasedthereby coagulating the particles together. As a result, the uniformlymixed polymer primary particles and inorganic particles are solidified.Then, by separating the co-aggregate from the aqueous medium and dryingthe co-aggregate, the polymer composition is obtained wherein theinorganic particles are uniformly dispersed at the nano level with theprimary particles of the polymer. On melting, compression molding, orsintering of the polymer, a composition is obtained wherein inorganicparticles are uniformly dispersed in the polymer at the nano level, i.e.the inorganic particles are of nano dimensions (1000 nm and smaller inparticle size) in the polymer matrix. Therefore, the present inventioncan be used in a variety of fields that require inorganic particles tobe uniformly dispersed at the nano level in a polymer matrix.

Another preferred embodiment of the present invention is the polymercomposition derived from this method wherein inorganic particles areuniformly dispersed at the nano level in the polymer. By derived ismeant directly obtained from the method, i.e. the co-aggregates, orindirectly obtained by processing of the co-aggregates, to make e.g.granules, pellets, or molded articles such as by compression molding ormelt mixing fabrication.

A preferred embodiment of the present invention is the granulated powderwhich is obtained by granulating the polymer composition.

A preferred embodiment of the present invention is the pellet which canbe obtained by melt-mixing in the course of extruding the polymercomposition or of the granulated powder of the polymer composition.

Another preferred embodiment of the present invention is the compositionobtained by melt-mixing the polymer composition derived by mixingpolymer dispersion comprising polymer primary particles with thecolloidal solution of inorganic articles, coagulating the resultantmixture to make a co-aggregate of the polymer primary articles with saidinorganic particles, separating said co-aggregate, and drying saidco-aggregate. The co-aggregate can be melt processed as such or aftergranulation or pelletization thereof. The melt mixing can also beapplied to the co-aggregate, granules, or pellets thereof. Compressionmolding is preferably carried out with the co-aggregates or granulesthereof.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a graph of the measurement of the zero shear rate viscosity ofpolymer compositions containing 20 wt % of silica.

FIG. 2 is a graph of the measurement of the zero shear rate viscosity ofthe polymer compositions containing 10 wt % and 20 wt % silica from PL-7silica sol.

FIG. 3 is an electron microscope picture of the cross section obtainedby fracture of a compression molding of the polymer composition sampleof Example 1.

FIG. 4 is an electron microscope picture of the cross section obtainedby fracture of a compression molding of the polymer composition sampleof Example 4.

FIG. 5 is an electron microscope picture of the surface of thedried-powder co-aggregate of Example 4.

FIG. 6 is an electron microscope picture of the cross section obtainedby fracture of a compression molding of the polymer composition sampleof Example 7.

FIG. 7 is an electron microscope picture of the surface a coating of thepolymer composition sample of in Comparative Example 2.

FIG. 8 is an electron microscope picture of the cross section obtainedby fracture of a compression molding of the polymer composition sampleof Comparative Example 3.

DETAILED DESCRIPTION OF THE INVENTION

The present invention provides a polymer composition wherein inorganicparticles are uniformly dispersed at the nano level in the polymer and amethod for manufacturing said polymer composition. The polymerdispersion used in the present invention is not limited to a specificdispersion and any polymer dispersion can be used. Fluoropolymers arethe preferred polymers. Examples of fluoropolymer dispersions includepolymer or copolymer of the monomers selected from tetrafluoroethylene(TFE), chlorotrifluoroethylene (CTFE), trifluoroethylene,hexafluoropropylene (HFP), perfluoro(alkyl vinyl ether) (PAVE), whichincludes perfluoro(methyl vinyl ether) (PMVE), perfluoro(ethyl vinylether) (PEVE), perfluoro(propyl vinyl ether) (PPVE), vinylidene fluoride(VdF or VF2)) and vinyl fluoride (VF), or a copolymers of the abovemonomers with ethylene or propylene.

Examples of the fluoropolymer dispersion include polytetrafluoroethylene(hereinafter called PTFE), TFE/PAVE copolymer (which hereinafter may becalled PFA, a species of which is sometimes called PMA if PMVE is amongthe monomers used), tetrafluoroethylene/ethylene copolymer (ETFE),polyvinylidene fluoride (PVDF), polychlorotrifluoroethylene (PCTFE),chlorotrifluoroethylene/ethylene copolymer (ECTFE), TFE/VdF copolymer,TFE/VF copolymer, TFE/HFP/VF copolymer, HFP/VdF copolymer, VdF/CTFEcopolymer, TFE/VdF/CTFE copolymer and TFE/HFP/VdF copolymer.

Among them, in the copolymer of tetrafluoroethylene and perfluoro(alkylvinyl ether), the number of carbons of alkyl group is preferably 1 to 5,or more preferably, 1 to 3. It is preferable that the dispersion of theabove described polymers and copolymers is manufactured by emulsionpolymerization.

According to the present invention, polymer dispersion wherein thepolymer primary particles are surrounded by a surfactant and stablydispersed in the dispersing liquid in the course of emulsionpolymerization, is mixed with a colloidal solution wherein inorganicparticles are stably dispersed and the polymer primary particles arethereby uniformly mixed with the inorganic particles. This mixture isstable since while the polymer primary particles and the inorganicparticles are interdispersed within the aqueous medium derived from theaqueous dispersion and the colloid, these particles are not attracted toone another to cause aggregation. The mixing and coagulation steps, thelatter causing co-aggregation, are sequentially, not simultaneouslycarried out. To cause coagulation, the stability of the colloid solutionis decreased, such as by shearing or other means disclosed herein.Therefore, it is possible to obtain a polymer composition wherein theinorganic particles and the polymer primary particles are uniformlydispersed at the nano level regardless of the chemical composition ofthe primary particles in the polymer dispersion. As a result, other thanthe above described fluoropolymer dispersion, it is possible to use manykinds of polymer dispersion, especially those obtainable by emulsionpolymerization.

Polymer dispersions may be made by other methods, such as by melting thepolymer and dispersing it, usually by mechanical action, such as highshear mixing, in a medium, such as water, usually with the aid of asurfactant (U.S. Pat. No. 2,995,533). Alternatively, polymer may bedissolved in a solvent, this solution dispersed in water with the aid ofa surfactant, and then the solvent removed by evaporation or bystripping, such as with steam.

Examples of preferred non-fluorine-containing polymer dispersion includepolystyrene (PS), poly(methyl methacrylate) (PMMA), poly(vinyl chloride)(PVC), polyisoprene, polybutadiene, styrene/butadiene copolymer (SBR),acrylonitrile/butadiene copolymer, methyl methacrylate/butadienecopolymer, 2-vinylpyridine/styrene/butadiene copolymer,acrylonitrile/butadiene/styrene copolymer, poly(vinyl acetate) (PVAc),and ethylene-vinyl acetate (EVAc).

The preferred particle diameter of the polymer primary particle in thepolymer dispersion depends on the particle diameter of the inorganicparticle in the colloid solution. For example, the average polymerprimary particle will generally be 50 to 500 nm, and preferably, 70 to300 nm.

The present invention uses colloidal solutions, also known as sols,wherein inorganic particles are stably dispersed. Examples of theinorganic particles of the sol include metals, including silica, andmetal compounds such as metal oxides, nitrides, zirconates silicates,antimonates, titanates, and hydroxides. It is preferable to use siliconoxide (SiO₂), titanium oxide (TiO₂), zeolite, zirconium oxide (ZrO₂),alumina (Al₂O₃), and zinc antimonate (ZnSb₂O₆). These materials may beused singly, or in combination of two or more. Examples of the othersuitable particles include silicon carbide (SiC), aluminum nitride(AlN), silicon nitride (Si₃N₄), barium titanate (BaTiO₃), boron nitride,lead oxide, tin oxide, chrome oxide, chromium hydroxide, cobalttitanate, cerium oxide, magnesium oxide, cerium zirconate, calciumsilicate, zirconium silicate, and transition metals, including gold,silver, and copper. The only limitation is that the particles becompatible with the components of the dispersion, such as the aqueousmedium, and the composition. The most preferred inorganic particles aresilicon oxide, titanium oxide, aluminum oxide, and zinc antimonate.

It is preferable that the inorganic particle sol of the presentinvention is stabilized in a liquid state by a variety of electrolyteand organic additives. For example, colloidal silica sol is a colloidsolution wherein negatively-charged silicon oxide nano particles aredispersed in water with silanol hydroxyl groups present in the surfaceof the particles. The inorganic particles are hydrophilic and are nottreated to make them porous.

The particle diameter of the inorganic particles of the sol normallyaverages 1 to 1000 nm, preferably, 5 to 500 nm, and more preferably, 10to 300 nm. Generally, for ease of preparation, sols having inorganicparticles with an average particle diameter of 5 to 500 nm arepreferred. For best uniform dispersion of inorganic particles at thenano level, it is especially preferable to use inorganic particle solhaving inorganic particles with an average particle diameter of 10 to300 nm. The colloids used in the present invention, although containinginorganic particles, are considered to be solution because the sol,generally at the usual low concentration of the inorganic particles inthe aqueous medium of the sol, has the transparency of water, i.e. theparticles are not visible to the naked eye.

Any of the known methods for coagulating polymer dispersions may beused. For example after the polymer dispersion is mixed with the sol,the mixture may be subjected to strong shearing using a stirring devicethereby coagulating the particles (physical coagulation). Another methodof physical coagulation is the freeze-thaw method. The mixture is cooledsufficiently to freeze it. This destabilizes the dispersion so that onthawing, the coagulate, which is the co-aggregate of the invention,separates from the liquid. Also, there is a method wherein anelectrolyte is added to the mixture so that the stability of the mixtureof polymer dispersion or the inorganic particle colloid solution isdecreased thereby causing coagulation (chemical or electrolytecoagulation). Among these methods, it is preferable to use the chemicalcoagulation method wherein an electrolyte such as nitric acid orinorganic salt is added to the mixture of polymer dispersion andinorganic particle sol so that the stability is decreased and theuniform mixture of the polymer primary particles and the inorganicparticles is solidified thereby obtaining co-aggregate wherein inorganicparticles and the primary polymer particles are uniformly dispersed.

There are a variety of electrolytes used for the chemical coagulationmethod depending on the type or ratio of the polymer primary particlesor inorganic particles in the mixed solution before they are chemicallycoagulated. Examples of the electrolytes which are used to chemicallycoagulate fluoropolymer primary particles in a fluoropolymer aqueousdispersion include inorganic or organic compounds such as aqueous HCl,H₂SO₄, HNO₃, H₃PO₄, Na₂SO₄, and MgCl₂. Among the above describedcompounds, it is preferable to use compounds which can volatilize duringthe process of drying the co-aggregate which is later conducted, such asHCl, HNO₃ and also, (NH₄)₂CO₃, and ammonium carbonate.

Furthermore, other than the above described electrolytes, it is possibleto use inorganic salts such alkali metal salt, alkaline earth metalsalt, and ammonium salt, of nitric acid, hydrohalic acid, phosphoricacid, sulfuric acid, molybdic acid, sulfuric acid, and preferably,potassium bromide, potassium nitrate, potassium iodide (KI), ammoniummolybdate, monobasic or dibasic sodium phosphate, ammonium bromide(NH₄Br), potassium chloride, calcium chloride, copper chloride andcalcium nitrate. The above described electrolytes can be independentlyused or in combinations of two or more. By repeatedly eluting theresulting co-aggregate with pure water and then drying, it is possibleto remove the inorganic salt from the co-aggregate.

It is preferable to use 1 to 50 wt %, more preferably 1 to 30 wt % ofthe above described electrolyte to the weight of the polymer, morepreferably, 1.5 to 30 wt %. It is also preferable to use 0.01 wt % to 30wt %, more preferably 0.02 wt % to 10 wt % of the above describedelectrolyte. Also, it is preferable to add the electrolyte in the formof an aqueous solution to the mixed solution of polymer dispersion andsol. If the amount of the electrolyte is too small, coagulation occursgradually and incompletely. As a result, it may not be possible tosolidify rapidly enough to ensure that the uniformly mixed state of thepolymer primary particles and the inorganic particles will persistthrough coagulation so as to ensure a co-aggregate wherein the inorganicparticles and primary polymer particles are uniformly mixed.

The device for mixing and coagulating the particles wherein the polymerdispersion is mixed with the inorganic particles and after the polymerprimary particles are uniformly mixed with the inorganic particles, andan electrolyte or inorganic salt is added to the mixture, is not limitedto a specific type. However, it is preferable to use a device which isequipped with a stirring means such as propeller blades, turbine blades,paddle blades, shell-shaped blades, horseshoe-shaped blades orspiral-shaped blades, in which the stirring speed can be controlled. Thedevice should have a water-discharge means.

By adding the polymer dispersion, and inorganic particle sol to theabove described device and stirring, and then adding electrolyte such asinorganic salt to the mixture and stirring, the colloid particles or/andthe inorganic particles are coagulated to create a co-aggregate ofpolymer and inorganic particles which is then separated from the aqueousmedium. The aqueous medium is separated from the co-aggregate and thensaid co-aggregate is washed with water so as to reduce electrolyteresidue to levels suitable for the intended use of the co-aggregate. Theseparation step is the recovery of the co-aggregate. After washing, theco-aggregate is dried at a temperature below the melting point of thepolymer and the below the temperature at which thermal decompositionstarts. It is preferable that the temperature at which the co-aggregateis dried is not so high that thermal degradation and thermaldecomposition of the polymer will occur, but high enough so thatvolatile electrolyte and surfactant will be vaporized. Drying conditionsshould include ventilation adequate to carry volatiles away. Theresulting dried co-aggregate is a powder wherein each powder particlecontains polymer primary particles and nano-sized inorganic particlesuniformly mixed.

The weight of inorganic particles in the mixture of the polymerdispersion and inorganic particle colloid, depending on the intended useof the polymer composition, is preferably 0.1 to 80 wt %, morepreferably, 0.3 to 50 wt %, and most preferably, 0.5 to 30 wt %, thebalance being the polymer in the dispersion, to total 100% of thecombined weights of polymer and inorganic particles. Thus, theco-aggregate and granules, pellets and articles molded therefrom thatcontain 0.1 to 80 wt % inorganic particles, will contain 99.9 to 20 wt %of the polymer either as primary particles or as polymer matrix obtainedtherefrom. In the nano polymer composition mixture or polymer nanocomposite according to this invention, wherein the inorganic particlesand primary polymer particles are uniformly dispersed at the nano level,when the composite is heated sufficiently to melt the polymer component,the interfacial area among the nano particles and the resulting polymermatrix is significantly increased compared with that of the conventionalpolymer compound mixture wherein filler is dispersed at a micro level,that is, where the filler particles are greater than about 1000 nm insize. Therefore, said polymer composition mixture has the advantagethat, even though the quantity of inorganic particles added is smallerthan that of the conventional polymer composition mixture, theproperties of the composite are improved.

One of the characteristics of the polymer composition mixture of thepresent invention wherein the polymer dispersion is mixed and stirredwith the sol where the inorganic particles are dispersed and the polymerprimary particles are uniformly mixed with the inorganic particles,which mixture is then coagulated thereby solidifying the uniformly mixedstate of the polymer primary particles and the inorganic particles, isthat, since the inorganic particles are uniformly dispersed at the nanolevel, after melting sintering or compression molding (as in a hotpress) of the polymer component, the resulting composition viscosity andelasticity are different from those of the conventional polymer mixtureswherein inorganic particles are of a size of several thousands ofnanometers or greater.

Concentrated solutions of polymer or molten polymer are typicallynon-Newtonian fluids and therefore their viscosities are dependent uponshear rate. As shear rate increases, viscosity decreases, and as shearrate decreases, viscosity increases. However, as the shear rate tendstowards zero, the viscosity approaches a constant value. This limitvalue is called “zero shear rate viscosity”. This is a most importantphysical value which indicates the viscosity of a polymer and is anexponential function of the polymer molecular weight.

For example, the melt viscosity of a melt processible fluoropolymernormally approaches a constant value as the shear rate is tends towardszero and shows a Newtonian fluid-like behavior (FIG. 1 (curve A)). Also,the viscosity of the conventional polymer composition mixture whereinfused silica with a particle diameter of about 3000 nm is dispersed inthe melt processible fluoropolymer, is greater by a constant factorcompared with the melt processible fluoropolymer to which silica is notadded. In this case, when the shear rate is decreased, the viscosityapproaches a constant value showing a Newtonian fluid-like behavior(FIG. 1 (curve B)). However, in the case of the melt processiblefluoropolymer composition of the present invention wherein silica with aparticle diameter of about 66 nm is uniformly dispersed in the meltprocessible fluoropolymer, when the shear rate is decreased, the meltviscosity does not approach a constant value. Instead, as the shear ratedecreases, the viscosity further increases (FIG. 1 (curve C) and (curveD)).

It is believed that the viscosity of the polymer composition mixture ofthe present invention continues to increase when the shear rate isdecreased because the activity of the surface of the nano particles issignificantly increased and at the same time the interfacial area amongthe nano particles and the polymer matrix is significantly increased,and the distance among the nano particles wherein nano particles areuniformly dispersed becomes shorter than is the case for conventionalpolymer composition mixtures wherein filler is dispersed at the micronlevel, i.e. >1000 nm. Silica with a particle diameter of 70 nmcompletely nano-dispersed in the polymer has a surface area of silica oralternatively, an interfacial area with the polymer, of about 400 timesgreater than the same weight of silica having a particle diameter ofabout 30000 nm.

The above described significant increase of the activity of the surfaceof the nano particles and their surface area or interfacial area is thecharacteristic of the polymer nano composite wherein inorganic particlesare dispersed at the nano level in the polymer and is believed to be thereason why properties are improved even though a smaller amount of theinorganic particles is used than would be the case for a conventionalpolymer composition mixture. For example, in the melt processiblefluoropolymer composition mixture wherein the inorganic nano particlesof the present invention are uniformly dispersed at the nano level, asthe shear rate decreases, the viscosity continues to increase.Therefore, the composition is especially suitable for use as insulationfor electric wire. Such insulation, when exposed to high heat, as in afire, is less likely than conventional compositions to drip. This isbecause of the viscosity-enhancing effect at low shear, such as theshear force of gravity, of the nano particle filler. Reduced dripping isdesirable because drops of molten polymer are hazardous, capable forexample of causing smoke and propagating fire.

Furthermore, the dispersive state of the nano particles in the polymercan be directly observed by an electron scanning microscope (SEM) ortransmission electron microscope (TEM). It is necessary use highermagnification with the nano particles than with convention fillers, andtherefore only the small local areas can be observed. As a result, it isdifficult to examine the dispersive state of all the nano particles in asample. However, by examining changes of the viscosity as the shear rateis increased, it is also possible to indirectly evaluate the dispersivestate of the nano particles.

In the case of the melt processible fluoropolymer composition which isobtained by mixing and stirring the polymer dispersion with theinorganic particle sol wherein the inorganic particles are dispersed,and then coagulating to obtain co-aggregate, followed by meltingsintering or compression molding of the polymer component, the meltviscosity is observed to vary with shear rate. The increase in meltviscosity with decreasing shear is preferably characterized by the ratio(V_(0.1)/V₁) of the melt viscosity (V_(0.1)) at 0.1 rad/sec to meltviscosity (V₁) at 1 rad/sec, viscosity being measured at 340° C. usingthe parallel-plate mode of a dynamic viscosity and elasticity measuringdevice. Depending on the relative amounts of the polymer primaryparticles and the inorganic particles, and the particle diameter of theinorganic particles, the ratio V_(0.1)/V₁ is preferably 1.4 or more, orpreferably, 1.5 or more, or more preferably, 2.0 or more.

In considering the ratio (D_(inorganic)/D_(polymer)) of the diameter ofthe inorganic particle (D_(inorganic)), to the polymer primary particle(D_(polymer)), when the mass of polymer in the composition is greaterthan that of inorganic material, the ratio (D_(inorganic)/D_(polymer))is preferably about 0.1 or greater, more preferably no less than about0.2, and most preferably no less than about 0.35. The ratio should notexceed 2.0. If the particle diameter of the inorganic particles is toosmall relative to the diameter of the primary polymer particle, thelarge polymer particles cannot cover or enclose (surround) the smallinorganic particles during coagulation, and the inorganic particles thustend to form their own large aggregates after coagulation, rather thanforming co-aggregate. In addition, if the diameter of the inorganicparticles is too large, the inorganic particles tend to settle under theinfluence of gravity. This can be a problem for the sol itself, and whenthe inorganic particle sol is mixed with the polymer dispersion. Thesame ratios are suitable for the case when the mass of polymer in thecomposition is greater than that of inorganic material.

According to the present invention, the co-aggregate of particleswherein the polymer primary particles and inorganic particles obtainedin the above described drying process, are uniformly dispersed, can bemelt-processed using known extrusion-molding methods, injecting-moldingmethods, compression molding methods, and transfer-molding methods. Suchprocessing is preferably done after the co-aggregate is pelletized,preferably in a melt extruder. Of course, the co-aggregate if notpelletized can be directly used in molding, or pelletized by compactingto improve feeding to the molding machine hopper. Also, the co-aggregateof the particles wherein the polymer primary particles and inorganicparticles obtained in the present invention are uniformly dispersed, canbe further granulated and used as the material for a powder molding,powder coating and rotomolding, which includes rotolining. One way inwhich such granulation can be achieved by post-coagulation addition of awater-immiscible solvent, as described in U.S. Pat. No. 4,675,380.

The co-aggregate, particularly the pelletized co-aggregate, may be usedas a “concentrate” to be blended with additional compatible polymer. Theresulting blend will have a lower concentration of filler, such assilica, if a silica sol is used in making the co-aggregate. By usingco-aggregate as concentrate, it is not necessary to make co-aggregatefor each polymer composite needed. The concentrate can be blended,preferably melt blended, if desired by first dry blending, such as dryblending of pellets of the composition with pellets of polymer, to givethe desired concentration of filler in the finished article.

Furthermore, when the co-aggregate is pelletized by using an extruder,it is preferable to use a twin-screw extruder because of its superiorshearing force. Also, during the process of pelletizing the co-aggregatein the extruder, it is possible to add additive(s) or to blend in otherpolymer(s). The addition of an additive can be done not only during themelt-extruding process but also during the process where the abovedescribed polymer dispersion and inorganic particle sol is mixed.Examples of additives include glass fiber, carbon fiber, aramide fiber,graphite, carbon black, mica, clay, fullerene, carbon nano tubes andcarbon nano fiber.

Because the particles are uniformly dispersed at the nano level in thepolymer, the final molded product can be used in a variety of areas toimprove properties. Examples of such molded product include tubes,sheets, films, rods, fabrics, fibers, packing, lining, seal rings,electric wire insulation, and film and print substrate. The polymercomposition in which the polymer itself is transparent and in which theuniformly dispersed inorganic are either small, or present in smallamount, or both, is also transparent. The inorganic nanoparticles arefrom 1 to 200 nm in size and are resent in concentrations of from 0.1 to40 wt % based on the combined weights of polymer and inorganicparticles. Such compositions are useful for a variety of purposes suchas a film for anti-reflective coatings, anti-scratch film, opticalfibers, transparent film, transparent tubes and electric material.Furthermore, since the particles are uniformly dispersed in the polymerand the shear rate is significantly decreased, the zero shear rateviscosity is significantly increased compared to the case where theparticles are not dispersed at the nano level. Therefore, the presentinvention can be also used for polymer products such as an electric wireinsulation because of increased resistance of the insulation to drip athigh heat, such as in a fire, because of the polymer high viscosityunder the low shear of gravity. This antidrip property is beneficialbecause it reduces the danger of dripping of the molten polymer underfire conditions.

EXAMPLES Example 1

The present invention is described in detail in the following Examples,which are not intended to be limiting.

(A. Measurement of the Properties) (1) Melting Point (Melting PeakTemperature)

A differential scanning calorimeter (Pyris 1 type DSC, made by PerkinElmer Co.) is used. About 10 mg of sample is weighed and placed in analuminum pan, which is then crimped. The crimped pan is placed in theDSC and the temperature is increased from 150° C. to 360° C. at 10°C./minute. The melting peak temperature (Tm) is obtained from themelting curve which is obtained in the above described process, beingthe maximum of the endotherm.

(2) Melt Flow Rate (MFR)

Using a melt indexer (made by Toyo Seiki Co.) equipped with corrosionresistant cylinder, die and piston which complies with ASTM D-1238-95, 5g of sample powder is put into the cylinder which is kept at 372±1° C.and maintained for 5 minutes. After that, the sample is extruded througha die orifice under 5 kg of load (piston plus weight) and the extrusionrate (g/10 minute) is the MFR. For PTFE, the molecular weight is toohigh to conduct a normal melt-extruding operation, therefore the meltflow rate is not measured.

(3) Particle Diameter

The particle diameter of the polymer primary particles in thefluoropolymer dispersion and of the silica particles in the silica solis obtained as follows: the concentration of the fluoropolymerdispersion or silica sol is diluted to 5 wt % by adding pure (deionizedor distilled) water, and dried. Then, the particles on the surface ofthe dried samples are observed by an electron microscope and the averageparticle diameters are obtained.

(4) Silica Dispersive State in the Polymer Matrix

A sheet having a thickness of about 200 μm is made bymelt-compression-molding at 350° C. fluoropolymer composition of theinvention. Sample pieces 10 mm×10 mm are cut from three sections of thesheet. Using an optical microscope (made by Nikon Co., OPTIPHOTO 2-POL),the dispersive state of the particles, that is, whether or not there areaggregates of silica nano particles of 1000 nm or more, is observed.

Samples in which the silica nano particles of 1000 nm or more areobserved, are placed in liquid nitrogen and fractured to exposecross-sectional surfaces. The exposed surfaces of three samples areobserved by electron microscope to evaluate the dispersive state ofsilica. The case where almost all of the silica is dispersed as primaryparticles is expressed by □. The case where only less than about 5% ofthe silica nano particles are aggregated to greater than 1000 nm areobserved is expressed by ∘. The case where a 20% or more of the silicanano particles are aggregated to greater than 1000 nm is expressed by x.

(5) Zero Shear Rate Viscosity

Sample pieces with a diameter of 25 mm are made from compression-molded(350° C.) sheet about 1.5 mm thick. Using a 25 mm-parallel plate in anARES viscosity and elasticity measuring device made by RheometricScientific Corporation (UK), the melt viscosity is measured at 340° C.over an oscillation frequency (shear rate) of 100 to 0.1 rad/sec, andthe ratio (V_(0.1)/V₁) of the melt viscosity (V_(0.1)) at 0.1 rad/sec tothe melt viscosity (V₁) at 1 rad/sec is calculated.

(6) Storage Elastic Modulus

Sample pieces of 12 mm×45 mm×1.5 mm are made from a compression-molded(350° C.) sheet of about 1.5 mm thick. Using an ARES viscosity andelasticity measuring device made by Rheometric Scientific Corporation,the storage elastic modulus is measured in torsion mode at 1 Hz from−40° C. to 200° C. at a heating rate of 5° C./minute.

(B. Materials)

The starting materials used in the examples of the present invention andthe comparative examples are described:

(1) PFA Emulsion

Made by DuPont Mitsui Fluorochemical Co. PFA aqueous dispersion isobtained by emulsion polymerization. Polymer solids: 30 wt %; averageparticle diameter of the PFA primary particles: 200 nm; pH 9; meltingpoint: 309° C.; and melt flow rate: 2 g/10 min.

(2) Pelletized PFA

(melting point: 309° C.; and melt flow rate: 2 g/10 minutes)

(3) PTFE Emulsion

(polymer solids: 50 wt %; average particle diameter of the primaryparticles: 210 nm; pH 9; and melting point: 326° C.)

(4) Silica Sol

(a) Made by Nissan Chemical Corporation, Snowtex MP2040 (silica: 40 wt%; silica primary particle diameter: 190 nm; and pH 9.5)(b) Made by Nissan Chemical Corporation, Snowtex MP1040 (silica: 40 wt%; silica primary particle diameter: 110 nm; and pH 9.5)(c) Made by Fuso Chemical Corporation, PL-7 (silica: 23 wt %; silicaprimary particle diameter: 70 nm; and pH 7.4)(d) Made by Fuso Chemical Corporation, PL-3 (silica: 20 wt %; silicaprimary particle diameter: 35 nm; and pH 7.2)

(5) Fused Silica

Made by Denki Kagaku Kogyo, FB-74 (silica average particle diameter:32000 nm)

Example 1

Silica sol, 33 g, made by Nissan Chemical Co. (MP-2040), and 1000 g ofpure water are placed in a beaker (2 L) which is stirred for 20 minutesat 200 rpm using a stirrer with four-blade down draft-type propeller.Then, 853 g of emulsion polymerized PFA aqueous dispersion is added tothe mixture so that the silica content becomes 5 wt % of the combinedweight of polymer and silica. After the mixture is stirred for another20 minutes, 9 ml of 60% aqueous nitric acid is added to the mixture.Said mixture is stirred again until it gels and fluoropolymer primaryparticles and silica nano particles are coagulated. The coagulatedco-aggregate is further stirred for 5 minutes at 350 rpm and thenseparated from the aqueous medium. After that, the co-aggregate is driedat 150° C. for 10 hours thereby obtaining an co-aggregate in adried-powder form. The dried co-aggregate powder is compression moldedat 350° C., giving a sheet having a thickness of about 1.5 mm.Elasticity and viscosity are measured and the sample is observed byusing an optical and electron microscopes. The results are summarized inTable 1 and in FIG. 3.

Example 2

Dried co-aggregate powder is made by the same procedure as that ofExample 1 except that the amount of the silica sol and the PFA aqueousdispersion is adjusted so that the silica content is 15 wt %. The driedco-aggregate powder is compression molded at 350° C. and, by using theresulting sheet having a thickness of about 1.5 mm, the elasticity andviscosity are measured. Results are summarized in Table 1.

Example 3

Dried co-aggregate powder is made by the same procedure as that ofExample 1 except that the amount of the silica sol and the PFA aqueousdispersion is adjusted so that the silica content is 20 wt %. The driedco-aggregate powder is compression molded at 350° C. and, using theresulting sheet having a thickness of about 1.5 mm, the elasticity andviscosity are measured and the sample is observed by using optical andelectron microscopes. The results are summarized in Table 1 and FIG. 1(curve C).

Example 4

Dried co-aggregate powder is made by the same procedure as that ofExample 1 except that PL-7 is used as the silica sol instead of MP-2040and the silica content is 10 wt %. The dried co-aggregate powder iscompression molded at 350° C. and, using the resulting sheet having athickness of about 1.5 mm, the elasticity and viscosity are measured andthe sample is observed using optical and electron microscopes. Theresults are summarized in Table 1 and FIGS. 2 (curve E) and 4. Also, toobserve the dispersed state of PFA particle and silica particle mixtureafter coagulation, the dried co-aggregate powder is further dried at295° C. for 12 hrs before being subjected to observation by electronmicroscopy. The results are shown in FIG. 5.

Example 5

Dried co-aggregate powder is made by the same procedure as that ofExample 4 except that the silica content is 20 wt % (PL-7). The driedco-aggregate powder is compression molded at 350° C. and, using theresulting sheet having a thickness of about 1.5 mm, the elasticity andviscosity are measured and the sample is observed by using optical andelectron microscopes. The results are summarized in Table 1 and FIGS. 1(curve D) and 2 (curve D).

Example 6

Dried co-aggregate powder is made by the same procedure as that ofExample 1 except that PL-3 is used as the silica sol instead of MP-2040and the silica content is 20 wt %. The dried co-aggregate powder iscompression molded at 350° C. and, using the resulting sheet having athickness of about 1.5 mm, the elasticity and viscosity are measured andthe sample is observed by using optical and electron microscopes. Theresults are summarized in Table 1.

Example 7

This Example uses PTFE that cannot be melt-processed. The driedco-aggregate powder is made by the same procedure as that of Example 1except that PTFE aqueous dispersion is used instead of PFA dispersion.The PTFE dispersion is diluted with pure water to a solids concentrationof 30 wt %. The silica content is 5 wt %. The melt viscosity of the PTFEis extremely high, so the viscosity is not measured. The driedco-aggregate powder is compression molded at 350° and, using theresulting sheet having a thickness of about 1.5 mm, the elasticity ismeasured and the sample is observed by using optical and electronmicroscopes. Because of the high viscosity of PTFE, viscosity is notmeasured. The results are summarized in Table 1 and FIG. 6.

Comparative Example 1

Fused silica with an average particle diameter of 32000 nm is melt-mixedwith pelletized PFA pellet using an R-60 melt-mixer (made by Toyo SeikiCo.) at 340° C. at 100 rpm for 5 minutes. This process gives aconventional composition wherein silica with an average particlediameter of 32000 nm is dispersed in the melt processible fluoropolymeris obtained. The silica content is 20 wt %. The resulting sample iscompression molded at 350° C. and, using the resulting sheet having athickness of about 1.5 mm, the elasticity and viscosity are measured andthe sample is observed by using an optical and electron microscopes. Theresults are summarized in Table 1 and FIG. 1 (curve B).

Comparative Example 2

In this example film is made by directly coating the solution offluoropolymer aqueous dispersion mixed with silica sol on a substrate.The mixed dispersion and sol is not coagulated. Silica sol, 33 g, madeby Nissan Chemical Co. (MP-1040) and 1000 g of pure water are placedinto a beaker (2 L) which is stirred for 20 minutes at 200 rpm by usinga down flow-type propeller four-blade stirring machine. PFA aqueousdispersion, 853 g, made by emulsion polymerization, is added to themixture so that a mixture having weight ratio of PFA to silica of 95/5is obtained. This mixture is then stirred for another 20 min. As aresult, a solution of fluoropolymer dispersion mixed with silica sol isobtained. The silica content is 5 wt %. The mixed solution is directlyspray-coated on an aluminum plate which is dried at 120° C. for 30minutes and sintered at 350° C. for 15 minutes, thereby obtaining acoated product with a coating thickness of about 50 μm. The surface ofthe coating product is observed by optical and electron microscopes andthe results are summarized in Table 1 and FIG. 7.

Comparative Example 3

In this example the mixed solution of the fluoropolymer dispersion andsilica sol is dried without being coagulated. Using the same method asin Example 4 except that MP-1040 is used as the silica sol instead ofMP2040, a mixed solution of the fluoropolymer aqueous dispersion andsilica sol wherein the silica content is 10 wt %, is obtained. The mixedsolution is dried at 80° C. for 12 hours thereby creating dried powder.The obtained dried co-aggregate powder is compression molded at 350° C.and, using the resulting sheet having a thickness of about 1.5 mm, theelasticity and viscosity are measured and the sample is observed byusing optical and electron microscopes. The results are summarized inTable 1 and FIG. 8.

Reference Example 1

The properties of the melt processible fluoropolymer itself, that iswithout added silica or other filler, are summarized in Table 1 andFIGS. 1 (curve A) and 2 (curve A).

Summary of Results from Examples

In Examples 1 to 3, the silica nano particles are completelynano-dispersed in the melt processible fluoropolymer matrix. Due to thenano-dispersed silica, the viscosity ratio (V_(0.1)/V₁) is higher thanthat of the pure melt processible fluoropolymer (Reference Example 1).As the silica content is increased, the viscosity ratio (V_(0.1)/V₁) isincreased. Also, as the amount of silica is increased, the storageelastic modulus is increased.

In Examples 4 and 5, the silica nano particles are completelynano-dispersed in the melt processible fluoropolymer matrix. Also,comparing the samples with silica is 20 wt % silica content, theviscosity ratio (V_(0.1)/V₁) is greater for Example 5 where the particlediameter of silica is smaller than that of Example 3. Especially, inExample 5, aggregates of silica particles are not observed on thesurface of the mixture wherein the PFA primary particles (averageparticle diameter: about 200 nm) and the silica particles (averageparticle diameter: about 70 nm) are coagulated before the driedco-aggregate powder is compression molded.

It is seen in Example 6, even in the case where the particle diameter ofsilica is 35 nm, the silica nano particles are completely nano-dispersedin the melt processible fluoropolymer matrix. Also, the aggregate madeof silica nano particles with a size of 1000 nm or more is not observedby an optical microscope. However, a few aggregates with a size of aboutseveral hundreds nm made of silica nano particles with a particlediameter of 35 nm are observed by an electron microscope at 20000-foldmagnification. Furthermore, the viscosity ratio (V_(0.1)/V₁) is almostthe same as that of Example 5 wherein the particle diameter is 70 nm andthe silica content is also 20%.

TABLE 1 Silica Primary Fluoropolymer particle volume (%) Weight diameterPFA PTFE (%) Type (nm) D_(inorganic)/D_(polymer) Example 1 95 — 5MP-2040 190 0.95 Example 2 85 — 15 MP-2040 190 0.95 Example 3 80 — 20MP-2040 190 0.95 Example 4 90 — 10 PL-7  70 0.35 Example 5 80 — 20 PL-7 70 0.35 Example 6 80 — 20 PL-3  35 0.175 Example 7 — 95 5 MP-2040 1900.95 Comparative 80 — 20 FB-74 (32000)  — Example 1 Comparative 95 — 5MP-1040 110 0.55 Example 2 Comparative 90 — 10 MP-1040 110 0.55 Example3 Referential 100 — — — — — Example 1 Properties of the compositionSilica Storage elastic modulus (Pa) V_(0.1) V₁ dispersive 25° C. 100° C.200° C. (Pa · s) (Pa · s) V_(0.1)/V₁ state Example 1 3.10E+08 1.00E+084.00E+07 31020 20110 1.54 □ Example 2 4.50E+08 1.60E+08 6.90E+07 7983739388 2.03 □ Example 3 6.10E+08 2.50E+08 1.10E+08 195070 62233 3.13 □Example 4 4.20E+08 1.40E+08 6.00E+07 80544 36946 2.18 □ Example 56.40E+08 2.80E+08 1.40E+08 455840 91241 5.00 ∘ Example 6 6.60E+083.20E+08 1.60E+08 1063700 156200 6.81 ∘ Example 7 Not measured Notmeasured □ Comparative 3.80E+08 1.20E+08 4.30E+07 39331 34553 1.14 xExample 1 Comparative Not measured Not measured x Example 2 Comparative3.30E+08 1.20E+08 4.50E+07 24048 17813 1.35 x Example 3 Reference2.40E+08 7.30E+07 2.80E+07 20864 18090 1.15 na Example 1 Note: “na”means not applicable

In Examples 3, 5 and 6, when the silica content is 20 wt %, as theparticle diameter of silica decreases, the storage elastic modulusincreases. In Example 7, since the melt viscosity of PTFE is very high,it is not practical to mix additives or nanoparticles with PTFE bymelt-mixing. The present invention offers a way to uniformly dispersesilica nanoparticles in the PTFE matrix.

Comparative Example 1 is the conventional polymer composition whereinsilica with an average particle diameter of 32000 nm is dispersed in themelt processible fluoropolymer. The viscosity ratio (V_(0.1)/V₁) isalmost the same as that of the melt processible fluoropolymer withoutsilica. This is because silica is not nano-dispersed and is noteffective in changing the viscosity ratio from that of the meltprocessible fluoropolymer alone.

In Comparative Example 2 a film is made by directly coating a substratewith the solution resulting from mixing of fluoropolymer dispersion withsilica sol. The co-aggregation step, e.g. coagulation with electrolyte,is omitted. Because there is no co-aggregation during the drying of themixed solution, the fluoropolymer primary particles and silica nanoparticles separate and cluster and the silica nano particles similarlycluster to a size of several micrometers, seen on the surface of thefilm after sintering.

The transparency of the polymer compositions of the Examples weredetermined, using pieces 50 mm×50 mm made from compression-molded (350°C.) sheet about 1 mm thick. Using a Haze-meter NDH2000 (Nippon Denshoku,Japan) equipped with a halogen lamp D65, the optical transmittance ofthe samples were measured. The averaged values of optical transmittancewere calculated from results of three sample pieces. Transmittances of50% or greater appear transparent to the naked eye.

Example 1 PFA with 5 wt % 190 nm silica had a transmittance of 50%.Examples 2 and 3 with 15 and 20 wt % respectively of 190 nm silica hadtransmittance of 30 and 20%, showing that 190 nm particles affecttransparency only at higher loadings. Examples 4 and 5 are PFA with 70nm silica at loadings of 10 and 20 wt % respectively have hightransmittance of 72 and 70%, showing that the smaller particles can beused at higher loadings without interfering with transparency. Example 6is PFA with a 20 wt % loading of 35 nm silica and has 70% transmittance.In Example 7, PTFE with 5% loading of 190 nm silica, i.e. the sameloading of the same sized silica as Example 1, has low transmittance,10%. This is the effect of the PTFE polymer, which being highlycrystalline, has low transparency, the crystals scattering light.

In conclusion, it is found that without co-aggregating it is notpossible to nano-disperse silica. To nano-disperse silica, it isnecessary to coagulate the mixed solution of the fluoropolymer aqueousdispersion and silica sol and solidify the uniformly mixed state of thepolymer primary particles and inorganic particle. In Comparative Example3, the mixed solution of the fluoropolymer aqueous dispersion and silicasol is not coagulated but rather directly dried. The result is theclustering of the silica nano particles (aggregation of silica particleswith each other).

According to the present invention, polymer dispersion wherein polymerprimary particles are surrounded by a surfactant and stably dispersed inthe solvent, such as by emulsion polymerization, is mixed and stirredwith a colloid solution and said inorganic particles are stablydispersed by a repulsive force among the inorganic particles. It is notnecessary to surface-treat the inorganic particles. After the polymerprimary particles and inorganic particles are uniformly mixed, thencoagulated by strong shearing using a mixer, by adding an electrolyte,or by freezing the dispersion. As a result, the stability of the polymerdispersion and that of the inorganic particle colloid solution isdecreased thereby coagulating the particles. As a result, the uniformlymixed state of the polymer primary particles and the inorganic particlesis solidified. Then, by separating the co-aggregated particles from thesolvent and drying, it is possible to obtain the polymer compositionwherein the inorganic particles are intimately mixed at the nano levelwith the polymer particles. Therefore, the present invention can be usedfor a variety of fields which benefit when the inorganic particles areuniformly dispersed at the nano level in polymer.

Furthermore, when the particles are uniformly dispersed in the moltenpolymer and the shear rate is significantly decreased, the zero shearrate viscosity is significantly increased compared with the case wherethe inorganic particles are not dispersed at the nano level. Therefore,the present invention can be also used for a polymer product such as anelectric wire insulation because of increased resistance of theinsulation to drip at high heat, such as in a fire, because of thepolymer's high viscosity under the low shear of gravity. This antidripproperty is beneficial because it reduces the danger of dripping moltenpolymer under fire conditions.

1. A method for making a polymer composition, comprising mixing aqueouspolymer dispersion comprising polymer primary particles with an aqueouscolloidal solution of spherical inorganic particles having an averagediameter of 10 to 300 nm, said inorganic particles being hydrophilic andstably dispersed in said solution, the ratio (D_(inorganic/)D_(polymer))of the average particle diameter (D_(inorganic)) of said inorganicparticles to the average primary particle diameter (D_(polymer)) of saidpolymer primary particles being 0.1 to 2.0, wherein said inorganicparticles are present in 0.1 to 40 wt % based on the combined weight ofsaid polymer and said inorganic particles coagulating the resultantmixture to make a co-aggregate of the polymer primary particles withsaid inorganic particles, separating said co-aggregate, and drying saidco-aggregate.
 2. The method claim 1 wherein said coagulating is achievedby shearing, adding electrolyte to, or freezing the resultant mixture.3. The method of claim 1 wherein said inorganic particles of saidcolloidal solution are selected from at least one of the groupconsisting of the silicon oxide, titanium oxide, aluminum oxide, andzinc antimonate.
 4. (canceled)
 5. The method of claim 1 wherein thepolymer of said polymer dispersion is a polymer or copolymer of monomerswhich are selected from the group consisting of tetrafluoroethylene,hexafluoropropylene, chlorotrifluoroethylene, perfluoro(alkyl vinylether), vinylidene fluoride and vinyl fluoride or a copolymer ofethylene or propylene with at least one of the monomers selected fromthe group consisting tetrafluoroethylene, hexafluoropropylene,chlorotrifluoroethylene, perfluoro(alkyl vinyl ether), vinylidenefluoride and vinyl fluoride.
 6. A polymer composition made by themethod, comprising mixing aqueous polymer dispersion comprising polymerprimary particles with an aqueous colloidal solution of sphericalinorganic particles having an average diameter of 10 to 300 nm, saidinorganic particles being hydrophilic and stably dispersed in saidsolution, the ratio (D_(inorganic)/D_(polymer)) of the average particlediameter (D_(inorganic)) of said inorganic particles to the averageprimary particle diameter (D_(polymer)) of said polymer primaryparticles being 0.1 to 2.0, wherein said inorganic particles are presentin 0.1 to 40 wt % based on the combined weight of said polymer and saidinorganic particles, coagulating the resultant mixture to make aco-aggregate of the polymer primary particles with said inorganicparticles, separating said co-aggregate, and drying said co-aggregate.7. The polymer composition of claim 6 wherein the ratio (V_(0.1)/V₁) ofthe melt viscosity (V_(0.1)) at 0.1 rad/sec to the melt viscosity (V₁)at 1 rad/sec is 1.4 or greater, said melt viscosities being measured at340° C. by the parallel-plate mode of a dynamic viscosity and elasticitymeasuring device.
 8. The polymer composition of claim 6 wherein thestorage elastic modulus at 200° C. is greater than 1.7 times than thatof the polymer or copolymer by itself.
 9. (canceled)
 10. A granulatedpowder which is obtained by granulating the polymer composition of claim6.
 11. A pellet which is obtained by melt-extruding the polymercomposition of claim
 6. 12. A composition obtained by melt-mixingpolymer composition derived from the method of claim
 1. 13. The methodof claim 1 further comprising melt processing said composition as saidco-aggregate, or as granules or pellets of said co-aggregate.
 14. Themethod of claim 1 further comprising compression molding saidcomposition as said co-aggregate, or as granules of said co-aggregate.15. A transparent molded article of the composition of claim
 6. 16.(canceled)
 17. The polymer composition of claim 6 wherein said aqueouscolloidal solution of inorganic particles is a silica sol. 18.(canceled)